Method for using sputtering target and method for forming oxide film

ABSTRACT

In a method for using a sputtering target, by making an ion collide with the sputtering target, a sputtered particle whose size is greater than or equal to 1/3000 and less than or equal to 1/20, preferably greater than or equal to 1/1000 and less than or equal to 1/30 of a crystal grain is generated.

BACKGROUND OF THE INVENTION

1. Field of the Invention

The present invention relates to a sputtering target and a method for using the sputtering target. Alternatively, the present invention relates to an oxide film formed by a sputtering method with use of the sputtering target, and a semiconductor device including the oxide film.

In this specification, a semiconductor device generally refers to a device which can function by utilizing semiconductor characteristics; an electro-optical device, a semiconductor circuit, and an electronic device are all included in the category of the semiconductor device.

2. Description of the Related Art

A technique by which a transistor is formed with a semiconductor thin film formed over a substrate having an insulating surface has been attracting attention. The transistor is applied to a wide range of electronic devices such as an integrated circuit (IC) or an image display device (display device). A silicon film is widely known as a semiconductor thin film applicable to the transistor. As another material, an oxide semiconductor film has been attracting attention.

For example, a transistor including an amorphous oxide semiconductor film that contains indium (In), gallium (Ga), and zinc (Zn) and has an electron carrier concentration lower than 10¹⁸/cm³ is disclosed. As a method for forming the amorphous oxide semiconductor film, a sputtering method is considered the most suitable (see Patent Document 1).

Although a transistor including an oxide semiconductor film containing a plurality of metal elements can obtain transistor characteristics relatively with ease, the oxide semiconductor film is likely to be amorphous and has unstable physical properties. Thus, it is has been difficult to secure reliability of such a transistor.

On the other hand, there is a report that a transistor including a crystalline oxide semiconductor film has more excellent electric characteristics and higher reliability than a transistor including an amorphous oxide semiconductor film (see Non-Patent Document 1).

REFERENCE Patent Document

-   [Patent Document 1] Japanese Published Patent Application No.     2006-165528

Non-Patent Document

-   [Non-Patent Document 1] Shunpei Yamazaki, Jun Koyama, Yoshitaka     Yamamoto, and Kenji Okamoto, “Research, Development, and Application     of Crystalline Oxide Semiconductor”, SID 2012 DIGEST, pp. 183-186

SUMMARY OF THE INVENTION

An object is to provide a method for using a sputtering target which enables formation of a crystalline oxide film containing a plurality of metal elements and having high orientation.

Another object is to provide a method for forming a crystalline oxide film having high orientation with use of the sputtering target.

One embodiment of the present invention is a method for using a sputtering target including a polycrystalline oxide containing a plurality of crystal grains. In the method for using a sputtering target, by making an ion collide with the sputtering target, a flat-plate-like sputtered particle is generated, and the flat-plate-like sputtered particle has a flat plane whose equivalent circle diameter is greater than or equal to 1/3000 and less than or equal to 1/20, preferably greater than or equal to 1/1000 and less than or equal to 1/30 of an average grain size of the plurality of crystal grains.

Another embodiment of the present invention is a method for using a sputtering target including a polycrystalline oxide containing a plurality of crystal grains each having a cleavage plane parallel to an a-b plane. In the method for using a sputtering target, by making an ion collide with the sputtering target, a sputtered particle which is cut out along the cleave plane and a plurality of planes perpendicular to the a-b plane is generated.

In this specification, the trigonal and rhombohedral crystal systems are included in the hexagonal crystal system. In this specification, a term “parallel” indicates that the angle formed between two straight lines is greater than or equal to −10° and less than or equal to 10°, and accordingly also includes the case where the angle is greater than or equal to −5° and less than or equal to 5°. In addition, a term “perpendicular” indicates that the angle formed between two straight lines is greater than or equal to 80° and less than or equal to 100°, and accordingly includes the case where the angle is greater than or equal to 85° and less than or equal to 95°.

Another embodiment of the present invention is a method for using a sputtering target including a polycrystalline oxide containing a plurality of crystal grains each having a cleavage plane parallel to an a-b plane. In the method for using a sputtering target, by making an ion generated from plasma collide with the sputtering target, part of the crystal grain is separated from the cleavage plane, and from the part of the crystal grain, a sputtered particle is generated by being cut out along a plurality of planes perpendicular to the a-b plane in plasma.

Note that the sputtered particle has a flat plane parallel to an a-b plane, and the equivalent circle diameter of the flat plane is greater than or equal to 1 nm and less than or equal to 15 nm, preferably greater than or equal to 2 nm and less than or equal to 10 nm. Here, the term “equivalent circle diameter of a flat plane” refers to the diameter of a perfect circle having the same area as the flat plane.

Further, an average grain size of the crystal grains is greater than or equal to 0.3 μm and less than or equal to 3 μm, preferably greater than or equal to 0.3 μm and less than or equal to 1 μm. Note that the average grain size of the crystal grains is obtained in the following manner: in a given cross section including a plurality of crystal grains, equivalent circle diameters of the respective crystal grains are calculated, and then the average of the equivalent circle diameters is figured out.

Another embodiment of the present invention is a method for forming an oxide film through deposition of sputtered particles with the method for using a sputtering target.

The cleavage plane indicates a plane where a bond of atoms or molecules constituting the crystal is weak (i.e., a plane where cleavage occurs or a plane which is easily cleaved).

According to one embodiment of the present invention, a sputtered particle is a flat-plate-like crystalline oxide particle having a flat plane parallel to an a-b plane. Thus, an oxide film formed through deposition of the sputtered particles is a crystalline oxide film with high orientation.

When the sputtered particle is too large, it is difficult to deposit the sputtered particle to obtain a uniform thickness of a deposited film. Thus, it is necessary that the equivalent circle diameter of a flat plane of a sputtered particle be sufficiently smaller than the average size of crystal grains of the polycrystalline oxide included in the sputtering target.

In a crystal grain of the polycrystalline oxide included in the sputtering target, a bond between a metal atom and an oxygen atom, which is the weakest bond, can be cut by impact of collision of an ion or by the action of plasma. By cutting the bond in the above manner, the equivalent circle diameter of a flat plane of the sputtered particle can be smaller than the average grain size of the crystal grains in the polycrystalline oxide included in the sputtering target.

By the method for using the sputtering target as described above, a crystalline oxide film with high orientation can be formed even when the oxide film contains a plurality of elements.

With use of a sputtering target including a polycrystalline oxide containing a plurality of crystal grains, a sputtered particle is separated from a cleavage plane of the crystal grain, so that a crystalline oxide film containing a plurality of metal elements and having high orientation can be formed.

BRIEF DESCRIPTION OF THE DRAWINGS

FIGS. 1A to 1C are schematic diagrams illustrating a situation where a sputtered particle is separated from a sputtering target.

FIG. 2 is a schematic diagram illustrating a situation where a sputtered particle is separated from a sputtering target.

FIGS. 3A and 3B are schematic diagrams illustrating a situation where a sputtered particle reaches a deposition surface and is deposited.

FIG. 4 is a flow chart showing an example of a method for forming a sputtering target.

FIGS. 5A and 5B are diagrams illustrating an example of a crystal structure of an In—Ga—Zn oxide.

FIG. 6 is a diagram illustrating an example of a crystal structure of an In—Ga—Zn oxide.

FIG. 7 is a top view illustrating an example of a film formation apparatus.

FIGS. 8A to 8C illustrate an example of a film formation apparatus.

DETAILED DESCRIPTION OF THE INVENTION

Hereinafter, embodiments of the present invention will be described in detail with reference to the accompanying drawings. However, the present invention is not limited to the description below, and it is easily understood by those skilled in the art that modes and details thereof can be modified in various ways. Therefore, the present invention is not construed as being limited to description of the embodiments. In describing structures of the present invention with reference to the drawings, the same reference numerals are used in common for the same portions in different drawings. Note that the same hatch pattern is applied to similar parts, and the similar parts are not especially denoted by reference numerals in some cases.

Note that the ordinal numbers such as “first” and “second” in this specification are used for convenience and do not denote the order of steps or the stacking order of layers. In addition, the ordinal numbers in this specification do not denote particular names which specify the present invention.

Note that an oxidizing atmosphere refers to an atmosphere containing an oxidizing gas. An oxidizing gas is oxygen, ozone, nitrous oxide, or the like, and it is preferable that the oxidizing gas do not contain water, hydrogen, and the like. For example, the purity of oxygen, ozone, or nitrous oxide introduced to a heat treatment apparatus is greater than or equal to 8N (99.999999%), preferably greater than or equal to 9N (99.9999999%). The oxidizing atmosphere may contain a mixed gas of an oxidizing gas and an inert gas. In that case, the atmosphere contains an oxidizing gas at a concentration at least higher than or equal to 10 ppm. Further, an inert atmosphere refers to an atmosphere containing an inert gas such as nitrogen or a rare gas or an atmosphere which does not contain a reaction gas such as an oxidizing gas. Specifically, in an inert atmosphere, the concentration of a reactive gas such as an oxidizing gas is lower than 10 ppm. Note that the pressure of each of the oxidizing atmosphere and the inert atmosphere may under reduced pressure that is lower than or equal to 100 Pa, lower than or equal to 10 Pa, or lower than or equal to 1 Pa.

Embodiment 1

In this embodiment, a method for using a sputtering target will be described.

FIG. 1A is a schematic view illustrating a situation where an ion 1001 collides with a sputtering target 1000, and a sputtered particle 1002 with crystallinity is generated. The sputtering target 1000 includes a polycrystalline oxide containing a crystal grain 1010. Note that the crystal grain 1010 has a grain size greater than or equal to 0.3 μm and less than or equal to 3 μm or greater than or equal to 0.3 μm and less than or equal to 1 μm.

Note that an oxygen cation is used as the ion 1001. Further, in addition to the oxygen cation, an argon cation may be used. Instead of the argon cation, a cation of another rare gas may be used. With use of an oxygen cation as the ion 1001, plasma damage at the film formation can be alleviated. Thus, when the ion 1001 collides with the surface of the sputtering target 1000, a lowering in crystallinity of the sputtering target 1000 can be suppressed or a change of the sputtering target 1000 into an amorphous state can be suppressed.

FIG. 1C illustrates a detailed situation where the sputtered particle 1002 is separated from the crystal grain 1010. According to FIG. 1C, the crystal grain 1010 has a cleavage plane 1005 parallel to a surface of the sputtering target 1000. Further, the crystal grain 1010 has a portion 1006 where an interatomic bond is weak (shown by a dotted line in the drawing). When the ion 1001 collides with the crystal grain 1010, an interatomic bond of the portion 1006 where an interatomic bond is weak is cut. Accordingly, the sputtered particle 1002 is separated in a flat-plate form by being cut out along the cleavage plane 1005 and the portion 1006 where an interatomic bond is weak. Note that the equivalent circle diameter of a flat plane of the sputtered particle 1002 is greater than or equal to 1/3000 and less than or equal to 1/20, preferably greater than or equal to 1/1000 and less than or equal to 1/30 of an average grain size of the crystal grains 1010.

Alternatively, part of the crystal grain 1010 is separated as a particle 1012 from the cleavage plane 1005. Then, when the particle 1012 is exposed to plasma, cutting of bonds starts at the portion 1006 where an interatomic bond is weak by an action of plasma, and a plurality of sputtered particles 1002 are generated (see FIG. 2).

Note that the sputtered particle 1002 may have a hexagonal prism shape with a flat plane parallel to an a-b plane. In such a case, a direction perpendicular to a hexagonal plane is a c-axis direction (see FIG. 1B). Note that the sputtered particle 1002 may have a triangular prism shape with a flat plane parallel to an a-b plane. Alternatively, the sputtered particle 1002 may have a polygonal prism shape different from the above. The sputtered particle 1002 has a flat plane whose equivalent circle diameter is greater than or equal to 1 nm and less than or equal to 15 nm, or greater than or equal to 2 nm and less than or equal to 10 nm.

It is preferable that the separated sputtered particles 1002 be positively charged. Alternatively there is no particular limitation on a timing of when the sputtered particle 1002 is positively charged, it is preferably positively charged by receiving an electric charge when the ion 1001 collides. Alternatively, in the case where plasma is generated, the sputtered particle 1002 is preferably exposed to plasma to be positively charged. Further alternatively, the ion 1001 which is an oxygen cation is preferably bonded to a surface of the sputtered particle 1002, whereby the sputtered particle 1002 is positively charged.

A situation where a sputtered particle is deposited on a deposition surface (a surface where a film is to be formed) is described with reference to FIGS. 3A and 3B. Note that in FIGS. 3A and 3B, sputtered particles which have been already deposited are shown by dotted lines.

In FIG. 3A, a deposition surface 1003 has a surface on which the sputtered particles 1002 are deposited. As shown in FIG. 3A, the sputtered particle 1002 is positively charged, and accordingly the sputtered particle 1002 is deposited on a region where other sputtered particles 1002 have not been deposited yet. This is because the sputtered particles 1002 that are positively charged repel each other.

An oxide film which is obtained by deposition has a uniform thickness and a uniform crystal orientation. The sputtered particles which are positively charged interact with each other and are deposited orderly so that c-axes are aligned in a direction perpendicular to the deposition surface.

FIG. 3B is a cross-sectional view taken along dashed-dotted line X-Y in FIG. 3A. An oxide film 1004 in which c-axes of crystals are aligned in a direction perpendicular to the deposition surface 1003 is, for example, a c-axis aligned crystalline oxide semiconductor (CAAC-OS) film.

The CAAC-OS film is one of oxide semiconductor films including a plurality of crystal parts, and most of the crystal parts each fit inside a cube whose one side is less than 100 nm. Thus, there is a case where a crystal part included in the CAAC-OS film fits inside a cube whose one side is less than 10 nm, less than 5 nm, or less than 3 nm. The density of defect states of the CAAC-OS film is lower than that of the microcrystalline oxide semiconductor film. The CAAC-OS film is described in detail below.

In a transmission electron microscope (TEM) image of the CAAC-OS film, a boundary between crystal parts, that is, a grain boundary is not clearly observed. Thus, in the CAAC-OS film, a reduction in electron mobility due to the grain boundary is less likely to occur.

According to the TEM image of the CAAC-OS film observed in a direction substantially parallel to a sample surface (cross-sectional TEM image), metal atoms are arranged in a layered manner in the crystal parts. Each metal atom layer has a morphology reflected by a surface over which the CAAC-OS film is formed (hereinafter, a surface over which the CAAC-OS film is formed is referred to as a formation surface) or a top surface of the CAAC-OS film, and is arranged in parallel to the formation surface or the top surface of the CAAC-OS film.

On the other hand, according to the TEM image of the CAAC-OS film observed in a direction substantially perpendicular to the sample surface (plan TEM image), metal atoms are arranged in a triangular or hexagonal configuration in the crystal parts. However, there is no regularity of arrangement of metal atoms between different crystal parts.

From the results of the cross-sectional TEM image and the plan TEM image, alignment is found in the crystal parts in the CAAC-OS film.

A CAAC-OS film is subjected to structural analysis with an X-ray diffraction (XRD) apparatus. For example, when the CAAC-OS film including an InGaZnO₄ crystal is analyzed by an out-of-plane method, a peak appears frequently when the diffraction angle (2θ) is around 31°. This peak is derived from the (009) plane of the InGaZnO₄ crystal, which indicates that crystals in the CAAC-OS film have c-axis alignment, and that the c-axes are aligned in a direction substantially perpendicular to the formation surface or the top surface of the CAAC-OS film.

On the other hand, when the CAAC-OS film is analyzed by an in-plane method in which an X-ray enters a sample in a direction substantially perpendicular to the c-axis, a peak appears frequently when 2θ is around 56°. This peak is derived from the (110) plane of the InGaZnO₄ crystal. Here, analysis (φ scan) is performed under conditions where the sample is rotated around a normal vector of a sample surface as an axis (φ axis) with 2θ fixed at around 56°. In the case where the sample is a single-crystal oxide semiconductor film of InGaZnO₄, six peaks appear. The six peaks are derived from crystal planes equivalent to the (110) plane. On the other hand, in the case of a CAAC-OS film, a peak is not clearly observed even when φ scan is performed with 2θ fixed at around 56°.

According to the above results, in the CAAC-OS film having c-axis alignment, while the directions of a-axes and b-axes are different between crystal parts, the c-axes are aligned in a direction parallel to a normal vector of a formation surface or a normal vector of a top surface. Thus, each metal atom layer arranged in a layered manner observed in the cross-sectional TEM image corresponds to a plane parallel to the a-b plane of the crystal.

Note that the crystal part is formed concurrently with deposition of the CAAC-OS film or is formed through crystallization treatment such as heat treatment. As described above, the c-axis of the crystal is aligned in a direction parallel to a normal vector of a formation surface or a normal vector of a top surface. Thus, for example, in the case where a shape of the CAAC-OS film is changed by etching or the like, the c-axis might not be necessarily parallel to a normal vector of a formation surface or a normal vector of a top surface of the CAAC-OS film.

Further, the degree of crystallinity in the CAAC-OS film is not necessarily uniform. For example, in the case where crystal growth leading to the CAAC-OS film occurs from the vicinity of the top surface of the film, the degree of the crystallinity in the vicinity of the top surface is higher than that in the vicinity of the formation surface in some cases. Further, when an impurity is added to the CAAC-OS film, the crystallinity in a region to which the impurity is added is changed, and the degree of crystallinity in the CAAC-OS film varies depending on regions.

Note that when the CAAC-OS film with an InGaZnO₄ crystal is analyzed by an out-of-plane method, a peak of 2θ may also be observed at around 36°, in addition to the peak of 2θ at around 31°. The peak of 2θ at around 36° indicates that a crystal having no c-axis alignment is included in part of the CAAC-OS film. It is preferable that in the CAAC-OS film, a peak of 2θ appear at around 31° and a peak of 2θ do not appear at around 36°.

In a transistor using the CAAC-OS film, change in electric characteristics due to irradiation with visible light or ultraviolet light is small. Thus, the transistor has high reliability.

With use of the sputtering target in the way as described above, an oxide film having a uniform thickness and a uniform crystal orientation can be formed.

FIG. 5A illustrates an example of the crystal structure of an In—Ga—Zn oxide viewed from a direction parallel to an a-b plane. Further, FIG. 5B illustrates an enlarged portion surrounded by a dashed line in FIG. 5A.

For example, in a crystal grain of an In—Ga—Zn oxide, a cleavage plane is a plane between a first layer and a second layer as illustrated in FIG. 5B. The first layer includes a gallium atom and/or zinc atom and an oxygen atom, and the second layer includes a gallium atom and/or zinc atom and an oxygen atom. This is because oxygen atoms having negative charge in the first layer and oxygen atoms having negative charge in the second layer are close to each other (see a portion surrounded by a dotted line in FIG. 5B). Since the cleavage plane is a flat plane parallel to an a-b plane, the sputtered particle including an In—Ga—Zn oxide has a flat-plate-like shape having a flat plane parallel to an a-b plane.

FIG. 6 illustrates an example of a crystal structure of an In—Ga—Zn oxide viewed from a direction perpendicular to an a-b plane of the crystal. Note that in FIG. 6, only a layer including indium atoms and oxygen atoms is extracted.

In the In—Ga—Zn oxide, a bond between an indium atom and an oxygen atom is weak and cut most easily. When the bond is cut, the oxygen atom is detached, and vacancies of oxygen atoms (also referred to as oxygen vacancy) are sequentially caused as shown by a dotted line in FIG. 6. In FIG. 6, a regular hexagonal shape can be traced by connecting the oxygen vacancies by the dotted line. As described above, the crystal of the In—Ga—Zn oxide has a plurality of planes which are perpendicular to an a-b plane and generated when the bonds between indium atoms and oxygen atoms are cut.

The crystal of the In—Ga—Zn oxide is a hexagonal crystal; thus the flat-plate-like sputtered particle is likely to have a hexagonal prism shape with a regular hexagonal plane whose internal angle is 120°. Note that the flat-plate-like sputtered particle is not limited to a hexagonal prism shape, and in some cases, it has a triangular prism shape with a regular triangular plane whose internal angle is 60° or a polygonal prism shape different from the above shapes.

By deposition of sputtered particles with use of the method for using a sputtering target described in this embodiment, a crystalline oxide film with high orientation can be formed.

Note that heat treatment is preferably performed on the deposited crystalline oxide film with high orientation in an oxidation atmosphere in order to reduce oxygen vacancies.

The oxide film described in this embodiment can be used for a transparent conductive film or a channel region of a transistor. With use of the oxide film described in this embodiment for a channel region of a transistor, the transistor can have excellent electric characteristics and high reliability.

This embodiment can be combined with the other embodiments as appropriate.

Embodiment 2

In this embodiment, a sputtering target of one embodiment of the present invention will be described.

FIG. 4 shows a method for forming a sputtering target.

First, raw materials are weighed in a step S101. As the raw materials, first to n-th (n is a natural number greater than or equal to 2) oxide powders are used. For example, an indium oxide powder, a gallium oxide powder, and a zinc oxide powder are used. Note that instead of the gallium oxide powder, a tin oxide powder, an aluminum oxide powder, a titanium oxide powder, a nickel oxide powder, a zirconium oxide powder, a lanthanum oxide powder, a cerium oxide powder, a neodymium oxide powder, a hafnium oxide powder, a tantalum oxide powder, or a tungsten oxide powder may be used. In this embodiment, the molar ratio of the indium oxide powder to the gallium oxide powder and the zinc oxide powder is 2:2:1, 8:4:3, 3:1:1, 1:1:1, 4:2:3, 1:1:2, 3:1:4, or 3:1:2. With such a molar ratio, a sputtering target including a polycrystalline oxide with high crystallinity can be easily obtained later.

However, a raw material used in this embodiment is not limited to the above raw materials. For example, the following raw materials may be used: an indium oxide powder and a zinc oxide powder; an indium oxide powder and a gallium oxide powder; a gallium oxide powder and a zinc oxide powder; an aluminum oxide powder and a zinc oxide powder; a zinc oxide powder and a tin oxide powder; or an indium oxide powder and a tin oxide powder.

Next, the weighed raw materials are mixed in a step S102.

Next, first baking is performed on the mixed raw material to obtain an oxide that is a reaction product. The first baking is performed in an inert atmosphere or an oxidizing atmosphere at a temperature higher than or equal to 700° C. and lower than or equal to 1700° C., preferably higher than or equal to 1200° C. and lower than or equal to 1700° C. The treatment time of the first baking may be, for example, longer than or equal to 1 hour and shorter than or equal to 72 hours, preferably longer than or equal to 9 hours and shorter than or equal to 72 hours, further preferably longer than or equal to 17 hours and shorter than or equal to 72 hours. In this embodiment, by the first baking, the indium oxide powder, the gallium oxide powder, and the zinc oxide powder are reacted to obtain an In—Ga—Zn oxide. Note that when the temperature of the first baking is higher than or equal to 700° C. and lower than or equal to 1700° C., preferably higher than or equal to 1200° C. and lower than or equal to 1700° C., crystallinity of the In—Ga—Zn oxide can be increased. Further, the longer the first baking time is, the lower the concentration of impurities contained in the In—Ga—Zn oxide can be. Note that when the baking time exceeds 72 hours, a change in crystallinity or a change in the impurity concentration is very small. Thus, for an improvement in productivity, it is preferable that the treatment time of the first baking be set to be shorter than or equal to 72 hours. However, it is acceptable to perform the first baking for 72 hours or longer.

Note that a time needed for temperature rising in the first baking is longer than or equal to 0 hours and shorter than or equal to 12 hours, preferably longer than or equal to 0 hours and shorter than or equal to 5 hours, further preferably longer than or equal to 0 hours and shorter than or equal to 2 hours. Further, a time needed for temperature decreasing in the first baking is longer than or equal to 0 hours and shorter than or equal to 12 hours, preferably longer than or equal to 0 hours and shorter than or equal to 5 hours, further preferably longer than or equal to 0 hours and shorter than or equal to 2 hours. When the time needed for temperature rising and the time needed for temperature decreasing in the first baking are made short, crystal grains contained in the In—Ga—Zn oxide can be small and are easily pulverized in a later step.

In this specification, the time needed for temperature rising indicates a time from when the temperature rising starts to when the temperature reaches 90% of the maximum temperature of baking. The treatment time of baking indicates a time from when the temperature becomes higher than or equal to 90% of the maximum temperature of baking to when the temperature decreases to be lower than 90% thereof. Further, the time needed for temperature decreasing indicates a time from when the temperature becomes lower than 90% of the maximum temperature of baking to when an object is taken out. For example, the time needed for temperature decreasing indicates a time when the temperature becomes lower than or equal to 150° C., lower than or equal to 100° C., or lower than or equal to 50° C.

The first baking may be performed plural times with different conditions. Specifically, it is preferable that after baking in an inert atmosphere is performed, baking be performed in an oxidation atmosphere. This is because in the case where the amount of impurities contained in an In—Ga—Zn oxide is reduced in an inert atmosphere, oxygen vacancies are caused in the In—Ga—Zn oxide. Thus, it is preferable that the oxygen vacancies caused in the In—Ga—Zn oxide be reduced in an oxidation atmosphere. By reducing the impurity concentration and oxygen vacancies, an In—Ga—Zn oxide with high crystallinity can be obtained.

As described above, the concentration of impurities contained in the In—Ga—Zn oxide can be reduced. Specifically, each of alkali metals can be lower than 10 ppm by weight, preferably lower than 5 ppm by weight, further preferably lower than 2 ppm by weight. Each of alkaline earth metals can be lower than 5 ppm by weight, preferably lower than 2 ppm by weight, further preferably lower than 1 ppm by weight. Halogen can be lower than 10 ppm by weight, preferably lower than 5 ppm by weight, further preferably lower than 2 ppm by weight. Boron, magnesium, phosphorus, copper, and germanium can be each lower than 5 ppm by weight, preferably lower than 2 ppm by weight, further preferably lower than 1 ppm by weight. Nitrogen can be lower than 20 ppm by weight, preferably lower than 10 ppm by weight, further preferably lower than 5 ppm by weight, still further preferably lower than 2 ppm by weight. Silicon can be lower than 50 ppm by weight, preferably lower than 20 ppm by weight, further preferably lower than 10 ppm by weight, still further preferably lower than 5 ppm by weight. Note that the concentration of impurities contained in the In—Ga—Zn oxide may be measured by secondary ion mass spectrometry (SIMS), glow discharge mass spectrometry (GDMS), inductively coupled plasma mass spectrometry (ICP-MS), or the like.

Next, an In—Ga—Zn oxide powder with crystallinity is obtained by grinding the In—Ga—Zn oxide in a step S104. A mill machine such as a ball mill may be used for grinding the In—Ga—Zn oxide. For a ball of the ball mill, a substance with a high degree of hardness such as agate, aluminum oxide, zirconium oxide, tungsten carbide, or silicon carbide may be used. There is no particular limitation on a container used for the ball mill. A substance that is the same as the ball is preferably used. Note that the treatment time for grinding in the ball mill is preferably longer than or equal to 8 hours and shorter than or equal to 72 hours, preferably longer than or equal to 20 hours and shorter than or equal to 72 hours.

Note that after the step S104 is performed, the process returns to the step S103, and the In—Ga—Zn oxide powder may be subjected to the first baking. In that case, after the first baking, the In—Ga—Zn oxide is ground again in the step S104. The step S103 and the step S104 are performed plural times, whereby crystallinity of the In—Ga—Zn oxide powder can be further increased.

Next, the grain size of the obtained In—Ga—Zn oxide powder is made uniform in a step S105. In this step, treatment is performed so that a grain size of the In—Ga—Zn oxide powder is less than or equal to 1 μm, preferably less than or equal to 0.5 μm, further preferably less than or equal to 0.3 μm. For this treatment, a sieve or a filter through which a particle with a size less than or equal to 1 μm, preferably less than or equal to 0.5 μm, further preferably less than or equal to 0.3 μm passes may be used. Then, an In—Ga—Zn oxide powder having a grain size less than 0.05 μm and low crystallinity is preferably removed. For removing such an oxide powder, a sieve or a filter through which a particle with a size less than 0.05 μm passes may be used. In the above manner, an In—Ga—Zn oxide powder whose grain size is greater than or equal to 0.05 μm and less than or equal to 1 μm, greater than or equal to 0.05 μm and less than or equal to 0.5 μm, or greater than or equal to 0.05 μm and less than or equal to 0.3 μm can be obtained.

Next, the In—Ga—Zn oxide powder is mixed with water and an organic substance (dispersing agent and binder) to obtain slurry in a step S106.

Next, the slurry is poured into a mold in a step S107. At least one suction port is provided at a bottom of the mold, which enables suction of water or the like. In addition, a filter is provided at the bottom of the mold. The filter has a function of inhibiting the In—Ga—Zn oxide powder to pass and allowing water and the organic substance to pass. Specifically, a filter in which a porous resin film is attached over a woven fabric or a felt may be used.

Next, in a step S108, water or the like is sucked from the slurry with the filter provided at the bottom of the mold, so that water and the organic substance are removed from the slurry and a molded body is formed.

Note that in the obtained molded body, water and the organic substance are slightly left; thus, drying treatment and a removal of the organic substance are performed in a step S109. The drying treatment is preferably natural drying because the molded body is less likely to be cracked. Further, the molded body is subjected to heat treatment at a temperature higher than or equal to 300° C. and lower than or equal to 700° C., so that residual water and organic substance which cannot be eliminated by natural drying are removed.

Next, the dried molded body from which the organic substance has been removed is subjected to pressure treatment in a step S110. In the pressure treatment, the molded body is preferably pressed, and for example, a weight is preferably used. Alternatively, the molded body may be pressed under high pressure using compressed air or the like. The pressure treatment performed on the molded body enables a crystal portion in the In—Ga—Zn oxide included in the molded body to have high orientation. Further, a void in the molded body can be made smaller.

Next, in a step S111, second baking is performed on the molded body which has been subjected to pressure treatment, so that a sintered body is formed. The second baking is performed in an inert atmosphere or an oxidation atmosphere at a temperature higher than or equal to 400° C. and lower than or equal to 1700° C., preferably higher than or equal to 400° C. and lower than or equal to 1400° C. The treatment time of the second baking may be, for example, longer than or equal to 1 hour and shorter than or equal to 72 hours, preferably longer than or equal to 9 hours and shorter than or equal to 72 hours, further preferably longer than or equal to 17 hours and shorter than or equal to 72 hours. In this embodiment, a void in the molded body can be made smaller by the second baking. When the temperature of the second baking is higher than or equal to 400° C. and lower than or equal to 1700° C., preferably higher than or equal to 400° C. and lower than or equal to 1400° C., the relative density of the sintered body is increased, and crystallinity of the In—Ga—Zn oxide in the sintered body can be increased. Further, when the second baking is performed at a lower temperature than that of the first baking, an excessive increase in the crystal grain size of the In—Ga—Zn oxide in the sintered body can be suppressed. However, it is acceptable to perform the second baking at a higher temperature than that of the first baking.

Note that a time needed for temperature rising in the second baking is longer than or equal to 12 hours and shorter than or equal to 240 hours, preferably longer than or equal to 24 hours and shorter than or equal to 240 hours, further preferably longer than or equal to 72 hours and shorter than or equal to 240 hours. Further, a time needed for temperature decreasing in the second baking is longer than or equal to 12 hours and shorter than or equal to 240 hours, preferably longer than or equal to 24 hours and shorter than or equal to 240 hours, further preferably longer than or equal to 72 hours and shorter than or equal to 240 hours. When the time needed for temperature rising and the time needed for temperature decreasing in the second baking are made longer, a crack is less likely to occur in the sintered body, so that a yield of the sputtering target can be improved. In addition, when the time needed for temperature rising and the time needed for temperature decreasing in the second baking are made longer, warpage or distortion of the sintered body is less likely to occur, so that a lowering in crystallinity of the In—Ga—Zn oxide in the sintered body can be suppressed.

The second baking may be performed plural times with different conditions. Specifically, it is preferable that after baking in an inert atmosphere is performed, baking be performed in an oxidizing atmosphere. This is because in the case where a void in the molded body is made smaller by the baking in the inert atmosphere, oxygen vacancies are caused in the In—Ga—Zn oxide included in the molded body. Thus, it is preferable to reduce, in the oxidation atmosphere, the oxygen vacancies caused in the In—Ga—Zn oxide included in the molded body. By making the void smaller, the relative density of the sintered body can be increased. Further, by reducing the oxygen vacancies, crystallinity of the In—Ga—Zn oxide in the sintered body can be increased.

Next, in a step S112, finishing treatment is performed on the sintered body, so that a sputtering target is obtained. Specifically, the sintered body is divided or grounded so as to adjust the length, the width, and the thickness. Further, since abnormal discharge might occur when a surface of the sintered body has minute unevenness, polishing treatment is performed on the surface. The polishing treatment is preferably performed by chemical mechanical polishing (CMP).

Through the above steps, a sputtering target including a polycrystalline oxide having high orientation can be formed. Further, the sputtering target has high relative density. Specifically, the relative density of the sputtering target can be set to be higher than or equal to 90%, higher than or equal to 95%, higher than or equal to 99%. In addition, the sputtering target has high purity. Specifically, the proportion of main components of the sputtering target can be higher than or equal to 99.9 wt. % (3N), preferably higher than or equal to 99.99 wt. % (4N), further preferably higher than or equal to 99.999 wt. % (5N).

As the specific concentration of impurities in the sputtering target, each of alkali metals can be lower than 10 ppm by weight, preferably lower than 5 ppm by weight, further preferably lower than 2 ppm by weight. Each of alkaline earth metals can be lower than 5 ppm by weight, preferably lower than 2 ppm by weight, further preferably lower than 1 ppm by weight. Halogen can be lower than 10 ppm by weight, preferably lower than 5 ppm by weight, further preferably lower than 2 ppm by weight. Boron, magnesium, phosphorus, copper, and germanium can each be lower than 5 ppm by weight, preferably lower than 2 ppm by weight, further preferably lower than 1 ppm by weight. Nitrogen can be lower than 20 ppm by weight, preferably lower than 10 ppm by weight, further preferably lower than 5 ppm by weight, still further preferably lower than 2 ppm by weight. Silicon can be lower than 50 ppm by weight, preferably lower than 20 ppm by weight, further preferably lower than 10 ppm by weight, still further preferably lower than 5 ppm by weight.

With use of the sputtering target including a polycrystalline oxide with high orientation, which is described in this embodiment, a crystalline oxide film with high orientation can be formed. Further, with use of the oxide film, a transistor with excellent electric characteristics and high reliability can be manufactured.

This embodiment can be combined with the other embodiments as appropriate.

Embodiment 3

In this embodiment, a film formation apparatus for forming the oxide film with high crystallinity described in Embodiment 1 is described.

First, a structure of a film formation apparatus which allows the entry of few impurities into a film during film formation is described with reference to FIG. 7 and FIGS. 8A to 8C.

FIG. 7 is a top view schematically illustrating a single wafer multi-chamber film formation apparatus 4000. The film formation apparatus 4000 includes an atmosphere-side substrate supply chamber 4001 including a cassette port 4101 for holding a substrate and an alignment port 4102 for performing alignment of a substrate, an atmosphere-side substrate transfer chamber 4002 through which a substrate is transferred from the atmosphere-side substrate supply chamber 4001, a load lock chamber 4003 a where a substrate is carried and the pressure is switched from atmospheric pressure to reduced pressure or from reduced pressure to atmospheric pressure, an unload lock chamber 4003 b where a substrate is carried out and the pressure is switched from reduced pressure to atmospheric pressure or from atmospheric pressure to reduced pressure, a transfer chamber 4004 through which a substrate is transferred in a vacuum, a substrate heating chamber 4005 where a substrate is heated, and film formation chambers 4006 a, 4006 b, and 4006 c in each of which a target is placed for film formation.

Note that a plurality of the cassette ports 4101 may be provided as illustrated in FIG. 7 (in FIG. 7, three cassette ports 4101 are provided).

The atmosphere-side substrate transfer chamber 4002 is connected to the load lock chamber 4003 a and the unload lock chamber 4003 b, the load lock chamber 4003 a and the unload lock chamber 4003 b are connected to the transfer chamber 4004, and the transfer chamber 4004 is connected to the substrate heating chamber 4005 and the film formation chambers 4006 a, 4006 b, and 4006 c.

Gate valves 4104 are provided for connecting portions between chambers so that each chamber except the atmosphere-side substrate supply chamber 4001 and the atmosphere-side substrate transfer chamber 4002 can be independently kept under vacuum. Moreover, the atmosphere-side substrate transfer chamber 4002 and the transfer chamber 4004 each include a transfer robot 4103, with which a glass substrate can be transferred.

Further, it is preferable that the substrate heating chamber 4005 also serve as a plasma treatment chamber. The film formation apparatus 4000 enables a substrate to transfer without being exposed to the air between treatment and treatment; therefore, adsorption of impurities on the substrate can be suppressed. In addition, the order of film formation, heat treatment, or the like can be freely determined. Note that the number of the transfer chambers, the number of the film formation chambers, the number of the load lock chambers, the number of the unload lock chambers, and the number of the substrate heating chambers are not limited to the above, and the numbers thereof can be set as appropriate depending on the space for placement or the process conditions.

Next, FIG. 8A, FIG. 8B, and FIG. 8C are a cross-sectional view taken along dashed-dotted line X1-X2, a cross-sectional view taken along dashed-dotted line Y1-Y2, and a cross-sectional view taken along dashed-dotted line Y2-Y3, respectively, in the film formation apparatus 4000 illustrated in FIG. 7.

FIG. 8A is a cross section of the substrate heating chamber 4005 and the transfer chamber 4004, and the substrate heating chamber 4005 includes a plurality of heating stages 4105 which can hold a substrate. Note that although the substrate heating chamber 4005 including the seven heating stages 4105 is illustrated in FIG. 8A, one embodiment of the present invention is not limited to such a structure. The number of heating stages 4105 may be greater than or equal to one and less than seven. Alternatively, the number of heating stages 4105 may be greater than or equal to eight. It is preferable to increase the number of the heating stages 4105 because a plurality of substrates can be subjected to heat treatment at the same time, which leads to an increase in productivity. Further, the substrate heating chamber 4005 is connected to a vacuum pump 4200 through a valve. As the vacuum pump 4200, a dry pump or a mechanical booster pump can be used, for example.

As a heating mechanism which can be used for the substrate heating chamber 4005, a heating mechanism in which heating is performed by using a resistance heater or the like may be used, for example. Alternatively, a heating mechanism in which heating is performed by heat conduction or heat radiation from a medium such as a heated gas may be used. For example, RTA (rapid thermal anneal) treatment, such as GRTA (gas rapid thermal anneal) treatment or LRTA (lamp rapid thermal anneal) treatment, can be used. The LRTA treatment is treatment for heating an object by radiation of light (an electromagnetic wave) emitted from a lamp, such as a halogen lamp, a metal halide lamp, a xenon arc lamp, a carbon arc lamp, a high-pressure sodium lamp, or a high-pressure mercury lamp. The GRTA is a heat treatment using a high-temperature gas. An inert gas is used as a gas.

Moreover, the substrate heating chamber 4005 is connected to a refiner 4301 through a mass flow controller 4300. Note that although the refiner 4301 and the mass flow controller 4300 can be provided for each of a plurality of kinds of gases, only one refiner 4301 and one mass flow controller 4300 are described for easy understanding. As the gas introduced to the substrate heating chamber 4005, a gas whose dew point is −80° C. or lower, preferably −100° C. or lower can be used; for example, an oxygen gas, a nitrogen gas, and a rare gas (e.g., an argon gas) are used.

The transfer chamber 4004 includes the transfer robot 4103. The transfer robot 4103 includes a plurality of movable portions and an arm for holding a substrate and can transfer a substrate to each chamber. Further, the transfer chamber 4004 is connected to a vacuum pump 4200 and a cryopump 4201 through valves. With such a structure, evacuation can be performed using the vacuum pump 4200 when the pressure inside the transfer chamber 4004 is in the range of atmospheric pressure to low vacuum (approximately 0.1 Pa to several hundred Pa) and then, by switching the valves, evacuation can be performed using the cryopump 4201 when the pressure inside the transfer chamber 4004 is in the range of middle vacuum to ultra-high vacuum (0.1 Pa to 1×10⁻⁷ Pa).

Alternatively, two or more cryopumps 4201 may be connected in parallel to the transfer chamber 4004. With such a structure, even when one of the cryopumps is in regeneration, evacuation can be performed using any of the other cryopumps. Note that the above regeneration refers to treatment for discharging molecules (or atoms) entrapped in the cryopump. When molecules (or atoms) are entrapped too much in a cryopump, the evacuation capability of the cryopump is lowered; therefore, regeneration is performed regularly.

FIG. 8B shows a cross section of the film formation chamber 4006 b, the transfer chamber 4004, and the load lock chamber 4003 a.

Here, the details of the film formation chamber (sputtering chamber) are described with reference to FIG. 8B. The film formation chamber 4006 b illustrated in FIG. 8B includes a target 4106, an attachment protection plate 4107, and a substrate stage 4108. Note that here, a substrate 4109 is provided on the substrate stage 4108. Although not illustrated, the substrate stage 4108 may include a substrate holding mechanism which holds the substrate 4109, a rear heater which heats the substrate 4109 from the back surface, or the like.

Note that the substrate stage 4108 is held substantially perpendicularly to a floor during film formation and is held substantially parallel to the floor when the substrate is delivered. In FIG. 8B, the position where the substrate stage 4108 is held when the substrate is delivered is denoted by a dashed line. With such a structure, the probability that dust or a particle which might be mixed into a film being formed is attached to the substrate 4109 can be suppressed as compared to the case where the substrate stage 4108 is held parallel to the floor. However, there is a possibility that the substrate 4109 falls when the substrate stage 4108 is held perpendicularly (90°) to the floor; therefore, the angle of the substrate stage 4108 to the floor is preferably wider than or equal to 80° and narrower than 90°.

The attachment protection plate 4107 can suppress deposition of a particle which is sputtered from the target 4106 on a region where deposition is not needed. Moreover, the attachment protection plate 4107 is preferably processed to prevent accumulated sputtered particles from being separated. For example, blasting treatment which increases surface roughness may be performed, or roughness may be formed on the surface of the attachment protection plate 4107.

The film formation chamber 4006 b is connected to a mass flow controller 4300 through a gas heating system 4302, and the gas heating system 4302 is connected to a refiner 4301 through the mass flow controller 4300. With the gas heating system 4302, a gas to be introduced to the film formation chamber 4006 b can be heated to a temperature higher than or equal to 40° C. and lower than or equal to 400° C., preferably higher than or equal to 50° C. and lower than or equal to 200° C. Note that although the gas heating system 4302, the mass flow controller 4300, and the refiner 4301 can be provided for each of a plurality of kinds of gases, only one gas heating system 4302, one mass flow controller 4300, and one refiner 4301 are provided for easy understanding. As the gas introduced to the film formation chamber 4006 b, a gas whose dew point is −80° C. or lower, preferably −100° C. or lower can be used; for example, an oxygen gas, a nitrogen gas, and a rare gas (e.g., an argon gas) are used.

In the film formation chamber 4006 b, a facing-target-type sputtering device may be employed. In each of the above-described structures of the facing-target-type sputtering device, plasma is confined between the targets; therefore, plasma damage to a substrate can be reduced. Further, step coverage can be improved because an incident angle of a sputtered particle to the substrate can be made smaller depending on the inclination of the target.

Note that a parallel-plate-type sputtering device or an ion beam sputtering device may be provided in the film formation chamber 4006 b.

In the case where the refiner is provided just before the gas is introduced, the length of a pipe between the refiner and the film formation chamber 4006 b is less than or equal to 10 m, preferably less than or equal to 5 m, further preferably less than or equal to 1 m. When the length of the pipe is less than or equal to 10 m, less than or equal to 5 m, or less than or equal to 1 m, the effect of the release of gas from the pipe can be reduced accordingly. As the pipe of the gas, a metal pipe the inside of which is covered with an iron fluoride, an aluminum oxide, a chromium oxide, or the like may be used. With the above pipe, the amount of released gas containing impurities is made small and the entry of impurities into the gas can be reduced as compared with a SUS316L-EP pipe, for example. Further, a high-performance ultra-compact metal gasket joint (a UPG joint) is preferably used as a joint of the pipe. A structure where all the materials of the pipe are metals is preferable because the effect of the generated released gas or the external leakage can be reduced compared with a structure where resin or the like is used.

The film formation chamber 4006 b is connected to a turbo molecular pump 4202 and a vacuum pump 4200 through valves.

In addition, the film formation chamber 4006 b is provided with a cryotrap 4110.

The cryotrap 4110 is a mechanism which can adsorb a molecule (or an atom) having a relatively high melting point, such as water. The turbo molecular pump 4202 is capable of stably evacuating a large-sized molecule (or atom), needs low frequency of maintenance, and thus enables high productivity, whereas it has a low capability in evacuating hydrogen and water. Hence, the cryotrap 4110 is connected to the film formation chamber 4006 b so as to have a high capability in evacuating water or the like. The temperature of a refrigerator of the cryotrap 4110 is set to be lower than or equal to 100 K, preferably lower than or equal to 80 K. In the case where the cryotrap 4110 includes a plurality of refrigerators, it is preferable to set the temperature of each refrigerator at a different temperature because efficient evacuation is possible. For example, the temperatures of a first-stage refrigerator and a second-stage refrigerator may be set at 100 K or lower and 20 K or lower, respectively.

Note that the evacuation method of the film formation chamber 4006 b is not limited to the above, and a structure similar to that in the evacuation method described in the transfer chamber 4004 (the evacuation method using the cryopump and the vacuum pump) may be employed. Needless to say, the evacuation method of the transfer chamber 4004 may have a structure similar to that of the film formation chamber 4006 b (the evacuation method using the turbo molecular pump and the vacuum pump).

Note that in each of the above transfer chamber 4004, the substrate heating chamber 4005, and the film formation chamber 4006 b, the back pressure (total pressure) and the partial pressure of each gas molecule (atom) are preferably set as follows. In particular, the back pressure and the partial pressure of each gas molecule (atom) in the film formation chamber 4006 b need to be noted because impurities might enter a film to be formed.

In each of the above chambers, the back pressure (total pressure) is lower than or equal to 1×10⁻⁴ Pa, preferably lower than or equal to 3×10⁻⁵ Pa, further preferably lower than or equal to 1×10⁻⁵ Pa. In each of the above chambers, the partial pressure of a gas molecule (atom) having a mass-to-charge ratio (m/z) of 18 is lower than or equal to 3×10⁻⁵ Pa, preferably lower than or equal to 1×10⁻⁵ Pa, further preferably lower than or equal to 3×10⁻⁶ Pa. Further, in each of the above chambers, the partial pressure of a gas molecule (atom) having a mass-to-charge ratio (m/z) of 28 is lower than or equal to 3×10⁻⁵ Pa, preferably lower than or equal to 1×10⁻⁵ Pa, further preferably lower than or equal to 3×10⁻⁶ Pa. Moreover, in each of the above chambers, the partial pressure of a gas molecule (atom) having a mass-to-charge ratio (m/z) of 44 is lower than or equal to 3×10⁻⁵ Pa, preferably lower than or equal to 1×10⁻⁵ Pa, further preferably lower than or equal to 3×10⁻⁶ Pa.

Note that a total pressure and a partial pressure in a vacuum chamber can be measured using a mass analyzer. For example, Qulee CGM-051, a quadrupole mass analyzer (also referred to as Q-mass) manufactured by ULVAC, Inc. may be used.

Moreover, the above transfer chamber 4004, the substrate heating chamber 4005, and the film formation chamber 4006 b preferably have a small amount of external leakage or internal leakage.

For example, in each of the above transfer chamber 4004, the substrate heating chamber 4005, and the film formation chamber 4006 b, the leakage rate is less than or equal to 3×10⁻⁶ Pa·m³/s, preferably less than or equal to 1×10⁻⁶ Pa·m³/s. The leakage rate of a gas molecule (atom) having a mass-to-charge ratio (m/z) of 18 is less than or equal to 1×10⁻⁷ Pa·m³/s, preferably less than or equal to 3×10⁻⁸ Pa·m³/s. The leakage rate of a gas molecule (atom) having a mass-to-charge ratio (m/z) of 28 is less than or equal to 1×10⁻⁵ Pa·m³/s, preferably less than or equal to 1×10⁻⁶ Pa·m³/s. The leakage rate of a gas molecule (atom) having a mass-to-charge ratio (m/z) of 44 is less than or equal to 3×10⁻⁶ Pa·m³/s, preferably less than or equal to 1×10⁻⁶ Pa·m³/s.

Note that a leakage rate can be derived from the total pressure and partial pressure measured using the mass analyzer.

The leakage rate depends on external leakage and internal leakage. The external leakage refers to inflow of gas from the outside of a vacuum system through a minute hole, a sealing defect, or the like. The internal leakage is due to leakage through a partition, such as a valve, in a vacuum system or due to gas released from an internal member. Measures need to be taken from both aspects of external leakage and internal leakage in order that the leakage rate be lower than or equal to the above value.

For example, an open/close portion of the film formation chamber 4006 b can be sealed with a metal gasket. For the metal gasket, metal covered with an iron fluoride, an aluminum oxide, or a chromium oxide is preferably used. The metal gasket realizes higher adhesion than an O-ring, and can reduce the external leakage. Further, with use of the metal covered with an iron fluoride, an aluminum oxide, a chromium oxide, or the like which is in the passive state, the release of gas containing impurities released from the metal gasket is suppressed, so that the internal leakage can be reduced.

For a member of the film formation apparatus 4000, aluminum, chromium, titanium, zirconium, nickel, or vanadium, which releases a smaller amount of gas containing impurities, is used. Alternatively, for the above member, an alloy containing iron, chromium, nickel, and the like covered with the above material may be used. The alloy containing iron, chromium, nickel, and the like is rigid, resistant to heat, and suitable for processing. Here, when surface unevenness of the member is decreased by polishing or the like to reduce the surface area, the released gas can be reduced.

Alternatively, the above member of the film formation apparatus 4000 may be covered with an iron fluoride, an aluminum oxide, a chromium oxide, or the like.

The member of the film formation apparatus 4000 is preferably formed with only metal as much as possible. For example, in the case where a viewing window formed with quartz or the like is provided, it is preferable that the surface of the member be thinly covered with an iron fluoride, an aluminum oxide, a chromium oxide, or the like so as to suppress the released gas.

When an adsorbate is present in the film formation chamber, the adsorbate does not affect the pressure in the film formation chamber because it is adsorbed onto an inner wall or the like; however, the adsorbate causes a release of gas when the inside of the film formation chamber is evacuated. Therefore, although there is no correlation between the leakage rate and the evacuation rate, it is important that the adsorbate present in the film formation chamber be desorbed as much as possible and evacuation be performed in advance with use of a pump with high evacuation capability. Note that the film formation chamber may be subjected to baking for promotion of desorption of the adsorbate. By the baking, the rate of desorption of the adsorbate can be increased about tenfold. The baking should be performed at a temperature greater than or equal to 100° C. and less than or equal to 450° C. At this time, when the adsorbate is removed while an inert gas is introduced to the film formation chamber, the desorption rate of water or the like, which is difficult to desorb simply by evacuation, can be further increased. Note that the rate of desorption of the adsorbate can be further increased by heating of the inert gas to be introduced at substantially the same temperature as the temperature of the baking. Here, a rare gas is preferably used as an inert gas. Depending on the kind of a film to be formed, oxygen or the like may be used instead of an inert gas. For example, in the case of depositing an oxide, using oxygen which is the main component of the oxide is preferable in some cases.

Alternatively, treatment for evacuating the inside of the film formation chamber is preferably performed a certain period of time after a heated oxygen gas, a heated inert gas such as a heated rare gas, or the like is introduced to increase pressure in the film formation chamber. The introduction of the heated gas can desorb the adsorbate in the film formation chamber, and the impurities present in the film formation chamber can be reduced. Note that a positive effect can be achieved when this treatment is repeated 2 to 30 times inclusive, preferably 5 to 15 times inclusive. Specifically, an inert gas, oxygen, or the like at a temperature in the range of 40° C. to 400° C., preferably 50° C. to 200° C. is supplied to the film formation chamber, so that the pressure therein can be kept in the range of 0.1 Pa to 10 kPa, preferably 1 Pa to 1 kPa, further preferably 5 Pa to 100 Pa for longer than or equal to 1 minute and shorter than or equal to 300 minutes, preferably longer than or equal to 5 minutes and shorter than or equal to 120 minutes. After that, the inside of the film formation chamber is evacuated for longer than or equal to 5 minutes and shorter than or equal to 300 minutes, preferably longer than or equal to 10 minutes and shorter than or equal to 120 minutes.

The rate of desorption of the adsorbate can be further increased also by dummy film formation. Here, the dummy film formation refers to film formation on a dummy substrate by sputtering or the like, in which a film is formed on the dummy substrate and the inner wall of the film formation chamber so that impurities in the film formation chamber and an adsorbate on the inner wall of the film formation chamber are confined in the film. For a dummy substrate, a substrate which releases a smaller amount of gas is preferably used. By performing dummy film formation, impurity concentration in a film to be formed can be reduced. Note that the dummy film formation may be performed at the same time as the baking of the film formation chamber.

Next, the details of the transfer chamber 4004 and the load lock chamber 4003 a illustrated in FIG. 8B and the atmosphere-side substrate transfer chamber 4002 and the atmosphere-side substrate supply chamber 4001 illustrated in FIG. 8C are described. Note that FIG. 8C is a cross section of the atmosphere-side substrate transfer chamber 4002 and the atmosphere-side substrate supply chamber 4001.

For the transfer chamber 4004 illustrated in FIG. 8B, the description of the transfer chamber 4004 illustrated in FIG. 8A can be referred to.

The load lock chamber 4003 a includes a substrate delivery stage 4111. When a pressure in the load lock chamber 4003 a becomes an atmospheric pressure by being increased from a reduced pressure, the substrate delivery stage 4111 receives a substrate from the transfer robot 4103 provided in the atmosphere-side substrate transfer chamber 4002. After that, the load lock chamber 4003 a is evacuated into vacuum so that the pressure therein becomes a reduced pressure and then the transfer robot 4103 provided in the transfer chamber 4004 receives the substrate from the substrate delivery stage 4111.

Further, the load lock chamber 4003 a is connected to a vacuum pump 4200 and a cryopump 4201 through valves. For a method for connecting evacuation systems such as the vacuum pump 4200 and the cryopump 4201, the description of the method for connecting the transfer chamber 4004 can be referred to, and the description thereof is omitted here. Note that the unload lock chamber 4003 b illustrated in FIG. 7 can have a structure similar to that in the load lock chamber 4003 a.

The atmosphere-side substrate transfer chamber 4002 includes the transfer robot 4103. The transfer robot 4103 can deliver a substrate from the cassette port 4101 to the load lock chamber 4003 a or deliver a substrate from the load lock chamber 4003 a to the cassette port 4101. Further, a mechanism for suppressing entry of dust or a particle, such as high efficiency particulate air (HEPA) filter, may be provided above the atmosphere-side substrate transfer chamber 4002 and the atmosphere-side substrate supply chamber 4001.

The atmosphere-side substrate supply chamber 4001 includes a plurality of the cassette ports 4101. The cassette port 4101 can hold a plurality of substrates.

When an oxide film is formed with use of the above film formation apparatus, the entry of impurities into the oxide film can be suppressed. Further, when a film in contact with the oxide film is formed with use of the above film formation apparatus, the entry of impurities into the oxide film from the film in contact therewith can be suppressed.

Next, a method for forming a CAAC-OS film with use of the above film formation apparatus is described.

In order to form the oxide film, the sputtering target described in Embodiment 1 is used.

The surface temperature of the sputtering target is set to be lower than or equal to 100° C., preferably lower than or equal to 50° C., further preferably about room temperature (typically, 25° C.). In a sputtering apparatus for a large substrate, a sputtering target having a large area is often used. However, it is difficult to form a sputtering target for a large substrate without a juncture. In fact, a plurality of sputtering targets are arranged so that there is as little space as possible therebetween to obtain a large shape; however, a slight space is inevitably generated. When the surface temperature of the sputtering target increases, in some cases, Zn or the like is volatilized from such slight spaces, and the spaces might expand gradually. When the space expands, a metal of a backing plate or a metal used for adhesion might be sputtered and cause an increase in the impurity concentration. Thus, it is preferable that the sputtering target be cooled sufficiently.

Specifically, for the backing plate, a metal having high conductivity and a high heat dissipation property (specifically Cu) is used. The sputtering target can be cooled efficiently by making a sufficient amount of cooling water flow through a water channel which is formed in the backing plate.

The oxide film is formed in an oxygen gas atmosphere with a substrate heating temperature higher than or equal to 100° C. and lower than or equal to 600° C., preferably higher than or equal to 150° C. and lower than or equal to 550° C., further preferably higher than or equal to 200° C. and lower than or equal to 500° C. The thickness of the oxide film is greater than or equal to 1 nm and less than or equal to 40 nm, preferably greater than or equal to 3 nm and less than or equal to 20 nm. As the substrate heating temperature during the film formation is higher, the impurity concentration in the obtained oxide film is lower. Further, migration of sputtered particles on a deposition surface is likely to occur; therefore, the atomic arrangement in the oxide film is ordered and the density thereof is increased, so that a CAAC-OS film with a high degree of crystallinity is formed easily. Furthermore, when the film formation is performed in an oxygen gas atmosphere, plasma damage is alleviated and a surplus atom such as a rare gas atom is not contained in the oxide film, whereby a CAAC-OS film with a high degree of crystallinity is formed easily. Note that the film formation may be performed in a mixed atmosphere including an oxygen gas and a rare gas. In that case, the percentage of an oxygen gas is set to be higher than or equal to 30 vol. %, preferably higher than or equal to 50 vol. %, further preferably higher than or equal to 80 vol. %.

Note that in the case where the sputtering target includes Zn, plasma damage is alleviated by the film formation in an oxygen gas atmosphere; thus, an oxide film in which Zn is unlikely to be volatilized can be obtained.

The oxide film is formed under conditions in which the film formation pressure is lower than or equal to 0.8 Pa, preferably lower than or equal to 0.4 Pa, and the distance between the sputtering target and a substrate is less than or equal to 100 mm, preferably less than or equal to 40 mm, further preferably less than or equal to 25 mm. When the oxide film is formed under such a condition, the frequency of the collision between a sputtered particle and another sputtered particle, a gas molecule, or an ion can be reduced. That is, depending on the film formation pressure, the distance between the sputtering target and the substrate is made shorter than the mean free path of a sputtered particle, a gas molecule, or an ion, so that the concentration of impurities entered the film can be reduced.

For example, when the pressure is 0.4 Pa and the temperature is 25° C. (the absolute temperature is 298 K), a hydrogen molecule (H₂) has a mean free path of 48.7 mm, a helium atom (He) has a mean free path of 57.9 mm, a water molecule (H₂O) has a mean free path of 31.3 mm, an methane molecule (CH₄) has a mean free path of 13.2 mm, a neon atom (Ne) has a mean free path of 42.3 mm, a nitrogen molecule (N₂) has a mean free path of 23.2 mm, a carbon monoxide molecule (CO) has a mean free path of 16.0 mm, an oxygen molecule (O₂) has a mean free path of 26.4 mm, an argon atom (Ar) has a mean free path of 28.3 mm, a carbon dioxide molecule (CO₂) has a mean free path of 10.9 mm, a krypton atom (Kr) has a mean free path of 13.4 mm, and a xenon atom (Xe) has a mean free path of 9.6 mm Note that doubling of the pressure halves a mean free path and doubling of the absolute temperature doubles a mean free path.

The mean free path depends on pressure, temperature, and the diameter of a molecule (atom). In the case where pressure and temperature are constant, as the diameter of a molecule (atom) is larger, the mean free path is shorter. Note that the diameters of the molecules (atoms) are as follows: H₂: 0.218 nm; He: 0.200 nm; H₂O: 0.272 nm; CH₄: 0.419 nm; Ne: 0.234 nm; N₂: 0.316 nm; CO: 0.380 nm; O₂: 0.296 nm; Ar: 0.286 nm; CO₂: 0.460 nm; Kr: 0.415 nm; and Xe: 0.491 nm.

Thus, as the diameter of a molecule (atom) is larger, the mean free path is shorter and the degree of crystallinity is lowered due to the large diameter of the molecule (atom) when the molecule (atom) enters the film. For this reason, it can be said that, for example, a molecule (atom) whose diameter is larger than that of Ar is likely to behave as an impurity.

Next, heat treatment is performed. The heat treatment is performed under reduced pressure or in an inert atmosphere or an oxidation atmosphere. By the heat treatment, the impurity concentration in the CAAC-OS film can be reduced.

The heat treatment is preferably performed in a manner such that after heat treatment is performed under reduced pressure or in an inert atmosphere, the atmosphere is switched to an oxidation atmosphere with the temperature maintained and heat treatment is further performed. When the heat treatment is performed under reduced pressure or in an inert atmosphere, the impurity concentration in the CAAC-OS film can be reduced; however, oxygen vacancies are caused at the same time. By the heat treatment in an oxidation atmosphere, the caused oxygen vacancies can be reduced.

When heat treatment is performed on the oxide semiconductor film after the film formation in addition to the substrate heating in the film formation, the impurity concentration in the CAAC-OS film can be significantly reduced.

Specifically, the concentration of hydrogen in the CAAC-OS film, which is measured by secondary ion mass spectrometry (SIMS), can be set to be lower than or equal to 2×10²⁰ atoms/cm³, preferably lower than or equal to 5×10¹⁹ atoms/cm³, further preferably lower than or equal to 1×10¹⁹ atoms/cm³, still further preferably lower than or equal to 5×10¹⁸ atoms/cm³.

The concentration of nitrogen in the CAAC-OS film, which is measured by SIMS, can be set to be lower than 5×10¹⁹ atoms/cm³, preferably lower than or equal to 5×10¹⁸ atoms/cm³, further preferably lower than or equal to 1×10¹⁸ atoms/cm³, still further preferably lower than or equal to 5×10¹⁷ atoms/cm³.

The concentration of carbon in the CAAC-OS film, which is measured by SIMS, can be set to be lower than 5×10¹⁹ atoms/cm³, preferably lower than or equal to 5×10¹⁸ atoms/cm³, further preferably lower than or equal to 1×10¹⁸ atoms/cm³, still further preferably lower than or equal to 5×10¹⁷ atoms/cm³.

The amount of each of the following gas molecules (atoms) released from the CAAC-OS film can be less than or equal to 1×10¹⁹/cm³, preferably less than or equal to 1×10¹⁸/cm³ or less, which is measured by thermal desorption spectroscopy (TDS) analysis: a gas molecule (atom) having a mass-to-charge ratio (m/z) of 2 (e.g., hydrogen molecule), a gas molecule (atom) having a mass-to-charge ratio (m/z) of 18, a gas molecule (atom) having a mass-to-charge ratio (m/z) of 28, and a gas molecule (atom) having a mass-to-charge ratio (m/z) of 44.

A known measurement method of the amount of released oxygen atoms is referred to for a measurement method of the release amount using TDS analysis.

In the above manner, a CAAC-OS film with a high degree of crystallinity can be formed.

This embodiment can be combined with the other embodiments as appropriate. This application is based on Japanese Patent Application serial no. 2012-174563 filed with Japan Patent Office on Aug. 7, 2012, the entire contents of which are hereby incorporated by reference. 

What is claimed is:
 1. A method for using a sputtering target including a polycrystalline oxide containing a plurality of crystal grains, comprising: generating a flat-plate-like particle having a flat plane by making an ion collide with the sputtering target, wherein an equivalent circle diameter of the flat plane is greater than or equal to 1/3000 and less than or equal to 1/20 of an average grain size of the plurality of crystal grains.
 2. The method for using a sputtering target according to claim 1, wherein each of the crystal grains has an a-b plane, wherein the flat-plate-like particle has a flat plane parallel to the a-b plane, and wherein an equivalent circle diameter of the flat plane parallel to the a-b plane is greater than or equal to 1 nm and less than or equal to 20 nm.
 3. The method for using a sputtering target according to claim 1, wherein an average grain size of the crystal grains is greater than or equal to 0.3 μm and less than or equal to 3 μm.
 4. A method for forming an oxide film, comprising: depositing the flat-plate-like particle by the method for using a sputtering target according to claim
 1. 5. The method for using a sputtering target according to claim 1, wherein the flat-plate-like particle has crystallinity.
 6. A method for forming an oxide film, comprising: depositing the flat-plate-like particle by the method for using a sputtering target according to claim 1, so that the oxide film is formed, wherein the oxide film comprises crystals each having c-axis aligned in a direction substantially perpendicular to a top surface of the oxide film.
 7. A method for using a sputtering target including a polycrystalline oxide containing a plurality of crystal grains each having an a-b plane and a cleavage plane parallel to the a-b plane, comprising: generating a particle which is cut out along the cleavage plane and a plurality of planes perpendicular to the a-b plane by making an ion collide with the sputtering target.
 8. The method for using a sputtering target according to claim 7, wherein the particle has a flat plane parallel to the a-b plane, and wherein an equivalent circle diameter of the flat plane of the particle is greater than or equal to 1 nm and less than or equal to 20 nm.
 9. The method for using a sputtering target according to claim 7, wherein an average grain size of the crystal grains is greater than or equal to 0.3 μm and less than or equal to 3 μm.
 10. A method for forming an oxide film, comprising: depositing the particle by the method for using a sputtering target according to claim
 7. 11. The method for using a sputtering target according to claim 7, wherein the particle has crystallinity.
 12. A method for forming an oxide film, comprising: depositing the particle by the method for using a sputtering target according to claim 7, so that the oxide film is formed, wherein the oxide film comprises crystals each having c-axis aligned in a direction substantially perpendicular to a top surface of the oxide film.
 13. A method for using a sputtering target including a polycrystalline oxide containing a plurality of crystal grains each having an a-b plane and a cleavage plane parallel to the a-b plane, comprising: separating a part of one of the crystal grains from the cleavage plane by making an ion generated from plasma collide with the sputtering target; and generating particles from the part of one of the crystal grains separated from the cleavage plane by being cut out along a plurality of planes perpendicular to the a-b plane in the plasma.
 14. The method for using a sputtering target according to claim 13, wherein each of the particles has a flat plane parallel to the a-b plane, and wherein an equivalent circle diameter of the flat plane of each of the particles is greater than or equal to 1 nm and less than or equal to 20 nm.
 15. The method for using a sputtering target according to claim 13, wherein an average grain size of the crystal grains is greater than or equal to 0.3 μm and less than or equal to 3 μm.
 16. A method for forming an oxide film, comprising: depositing the particles by the method for using a sputtering target according to claim
 13. 17. The method for using a sputtering target according to claim 13, wherein each of the particles has crystallinity.
 18. A method for forming an oxide film, comprising: depositing the particles by the method for using a sputtering target according to claim 13, so that the oxide film is formed, wherein the oxide film comprises crystals each having c-axis aligned in a direction substantially perpendicular to a top surface of the oxide film. 